CN107429351A - The manufacture method and structural tube of structural tube steel plate, structural tube steel plate - Google Patents
The manufacture method and structural tube of structural tube steel plate, structural tube steel plate Download PDFInfo
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- CN107429351A CN107429351A CN201680017746.0A CN201680017746A CN107429351A CN 107429351 A CN107429351 A CN 107429351A CN 201680017746 A CN201680017746 A CN 201680017746A CN 107429351 A CN107429351 A CN 107429351A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 177
- 239000010959 steel Substances 0.000 title claims abstract description 177
- 238000000034 method Methods 0.000 title claims description 43
- 238000004519 manufacturing process Methods 0.000 title claims description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 38
- 239000000463 material Substances 0.000 claims abstract description 30
- 239000000203 mixture Substances 0.000 claims abstract description 23
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 22
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 21
- 238000001816 cooling Methods 0.000 claims description 33
- 238000010438 heat treatment Methods 0.000 claims description 14
- 230000008569 process Effects 0.000 claims description 14
- 238000005098 hot rolling Methods 0.000 claims description 11
- 238000003303 reheating Methods 0.000 claims description 11
- 230000001133 acceleration Effects 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 8
- 229910052799 carbon Inorganic materials 0.000 claims description 7
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 238000003032 molecular docking Methods 0.000 claims description 3
- 229910052757 nitrogen Inorganic materials 0.000 claims description 3
- 238000005275 alloying Methods 0.000 abstract description 6
- 230000000694 effects Effects 0.000 description 19
- 238000003466 welding Methods 0.000 description 18
- 229910052751 metal Inorganic materials 0.000 description 11
- 239000002184 metal Substances 0.000 description 11
- 239000008186 active pharmaceutical agent Substances 0.000 description 9
- 229910052761 rare earth metal Inorganic materials 0.000 description 9
- 229910052758 niobium Inorganic materials 0.000 description 7
- 150000002910 rare earth metals Chemical class 0.000 description 7
- 230000009467 reduction Effects 0.000 description 7
- 229910052719 titanium Inorganic materials 0.000 description 7
- 230000009466 transformation Effects 0.000 description 7
- 229910001566 austenite Inorganic materials 0.000 description 6
- 229910052698 phosphorus Inorganic materials 0.000 description 6
- 238000005476 soldering Methods 0.000 description 6
- 229910052717 sulfur Inorganic materials 0.000 description 6
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 5
- 239000010953 base metal Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 5
- 229910052750 molybdenum Inorganic materials 0.000 description 5
- 239000010813 municipal solid waste Substances 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 230000009471 action Effects 0.000 description 3
- 230000002411 adverse Effects 0.000 description 3
- 229910052804 chromium Inorganic materials 0.000 description 3
- 239000004020 conductor Substances 0.000 description 3
- 235000013399 edible fruits Nutrition 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 230000004907 flux Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 229910052759 nickel Inorganic materials 0.000 description 3
- 229910001562 pearlite Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910000859 α-Fe Inorganic materials 0.000 description 3
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 229910052802 copper Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 229910017604 nitric acid Inorganic materials 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 229910000679 solder Inorganic materials 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 230000000007 visual effect Effects 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- -1 REM REM Chemical class 0.000 description 1
- 208000037656 Respiratory Sounds Diseases 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 238000009412 basement excavation Methods 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910001567 cementite Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000000354 decomposition reaction Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 230000029052 metamorphosis Effects 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 239000003345 natural gas Substances 0.000 description 1
- 239000001301 oxygen Substances 0.000 description 1
- 239000003208 petroleum Substances 0.000 description 1
- 238000013001 point bending Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000009628 steelmaking Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000035899 viability Effects 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/02—Rigid pipes of metal
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/17—Rigid pipes obtained by bending a sheet longitudinally and connecting the edges
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The present invention provides a kind of structural tube steel plate, it is high-strength steel sheet more than API X100 grades, and in the case where not adding substantial amounts of alloying element rolling direction excellent strength, and rolling direction with rolling vertical direction intensity difference it is small (property uniform in material is excellent).Specifically, there is the structural tube steel plate specific composition to form, it is main body and microstructure of the Line Integral rate less than 3.0% of island-like martensite with bainite, the tensile strength of rolling direction is more than 760MPa, rolls the tensile strength (TS of orthogonal directionC) with the tensile strength (TS of rolling directionL) difference (TSC‑TSL) absolute value be below 30MPa.
Description
Technical field
The present invention relates to a kind of structural tube steel plate, the invention particularly relates to a kind of with more than API X100 grades strong
The excellent structural tube steel plate of the small property uniform in material of the intensity difference of degree and rolling direction and rolling vertical direction.
Moreover, it relates to what the manufacture method and the effective steel plate of use said structure of the effective steel plate of said structure manufactured
Structural tube.
Background technology
In the excavation using the oil or natural gas of the progress such as seabed resources drilling ship, conductor casing steel pipe is used
The structural tubes such as (conductor casing steel pipe), standpipe steel pipe (riser steel pipe).In these purposes
In, in recent years, raising from the operating efficiency risen based on pressure, from the viewpoint of the abatement of the cost of raw material is (beautiful to API
Petroleum institute of state) requirement of more than X100 grades high tensile steel tube improves.
In addition, the very more forged article of alloying element amount (such as connector etc.) is entered when structural tube is most as described above
Row circumference soldering and use.When being welded, for the residual stress for removing forged article caused by welding purpose and
Implement PWHT (Post Weld Heat Treatment, be heat-treated after welding), it is likely that causing intensity etc. because of heat treatment
The reduction of mechanical property.Therefore, excellent mechanical property is also required after PWHT to structural tube, especially for prevent because excavate
When seabed external pressure caused by destruction, it is desirable in the long side direction of pipe, i.e., rolling direction maintains high intensity.
Thus, for example proposed in patent document 1 by the addition of 0.30~1.00% Cr, 0.005~
0.0030% Ti and less than 0.060% Nb steel accelerate cooling after carrying out hot rolling, so as to manufacture the high temperature more than 600 DEG C
It can also remain excellent after belong to a kind of destressing (stress elimination, Stress Relief, SR) annealing in PWHT
The high intensity standpipe steel for steel pipes plate of intensity.
In addition, propose a kind of welded still pipe in patent document 2, wherein, make mother metal portion and welding metal into packet
Into respectively specific scope, and both yield strengths are made to be more than 551MPa.Above-mentioned weldering has been recorded in patent document 2
Connect tenacity excellent of the steel pipe before and after weld part its SR.
Prior art literature
Patent document
Patent document 1:Japanese Unexamined Patent Publication 11-50188 publications
Patent document 2:Japanese Unexamined Patent Publication 2001-158939 publications
The content of the invention
But in the steel plate described in patent document 1 because in PWHT by separate out Cr carbide make up because
Intensity decreases caused by PWHT, so needing to add substantial amounts of Cr.Therefore, not only the cost of raw material is high, and is likely to result in
Weldability or toughness reduce.
In addition, the steel pipe described in patent document 2 is mainly focused on the characteristic for improving seam weld metal, mother metal is not carried out
It is special to consider, the reduction of the strength of parent caused by PWHT can not be avoided.In order to ensure strength of parent, it is necessary to beforehand through control
System rolling accelerates cooling to improve the intensity before PWHT.
Should illustrate, due to it is set forth below the reasons why, to structural tube with steel plate require rolling direction with rolling vertical direction
Intensity difference it is small (property uniform in material is excellent).
That is, the intensity of the welded-joint (welding metal portion) of steel pipe is generally configured to higher than the intensity of steel pipe mother metal.Should
Design philosophy is also referred to as overmatch (over-matching).When the steel pipe of laying is deformed or destroyed because of certain reason, only
Overmatch is realized, then steel pipe mother metal turns into deformation or the starting point destroyed, rather than welded-joint.With welded-joint phase
Than the reliability of the viability of the material of steel pipe mother metal is high, therefore laid body can be improved by overmatch
Security.
It is also real in addition to the seam weld (seam welding) implemented when steel pipe is manufactured by steel plate in the case of for structural tube
Apply the circumference soldering (girth welding) for connecting each steel pipe.Therefore, seam weld connector portions and circumference soldering connector portions this two
Overmatch is needed in person.That is, it needs to the intensity of seam weld connector portions is higher than the intensity in the direction vertical with the rolling direction of steel plate,
And the intensity of circumference soldering connector portions is higher than the intensity of the rolling direction of steel plate.Here, the intensity of the rolling direction of steel plate and with
The difference of the intensity in the vertical direction of rolling direction is small, then can realize superpower of seam weld connector portions and circumference soldering connector portions
Match somebody with somebody, and almost identical or similar welding procedure method can be applied, thus preferably.
The present invention be in view of above-mentioned actual conditions and develop, and it is an object of the present invention to provide a kind of structural tube steel plate, is API
High-strength steel sheet more than X100 grades, the excellent strength of rolling direction in the case where not adding substantial amounts of alloying element, and
And the intensity difference of rolling direction and rolling vertical direction is small (property uniform in material is excellent).
It is in addition, it is an object of the invention to provide the manufacture method of the effective steel plate of said structure and effective using said structure
The structural tube of steel plate manufacture.
The present inventor etc. in order in structural tube with the property and intensity uniform in material of being got both in steel plate, with regard to rolling condition to steel plate
Influence caused by microstructure is studied in detail.Typically, from the viewpoint of weldability, the steel plate of welded still pipe or
The chemical composition of the steel plate of welding structure is severely limited, so high-strength steel sheet more than X65 grades passes through in hot rolling
Cooling is accelerated to manufacture afterwards.Therefore, the microcosmic composition of steel plate is that bainite is main body or contains island-like martensite in bainite
The tissue of (Martensite-Austenite constituent, below, being designated as sometimes " MA "), but if to such tissue
Steel implement PWHT, then the island-like martensite tissue in bainite is decomposed due to tempering, thus can not avoid the reduction of intensity.
In addition, though have to make up the method that Cr carbide etc. is separated out in PWHT because of the intensity decreases caused by tempering, but by
In the easy coarsening of carbide, toughness can reduce.So, it is known that intensity and tough is also ensured that after PWHT by phase transformation strengthening
The limit be present in the effect of property.Therefore, the present inventor etc. are on obtaining excellent resistance to PWHT and intensity and property uniform in material
Microstructure has made intensive studies, and has as a result obtained the opinion of following (a) and (b).
(a) in order to improve resistance to PWHT, it is necessary to make steel microstructure turn into metamorphosis is not produced before and after PWHT
Tissue.As long as therefore, reducing the amount of the island-like martensite decomposed by PWHT, and make the carbon in steel with heat-staple fine
The form of carbide is dispersed to precipitate.
(b) in order to obtain high intensity and the excellent steel plate of property uniform in material, as long as with to the greatest extent in acceleration cooling after hot rolling
Temperature that may be low stops cooling, then, rapid heating immediately.Stop microcosmic group of the steel after above-mentioned acceleration cooling at once
It is made into as the bainite structure that MA is few, dislocation density is high, but fixed by reheating thereafter to make mobile dislocation by solid solution C
As a result, it is possible to obtain the excellent steel plate of property uniform in material.
Based on above opinion, composition composition, microstructure and the manufacturing condition of steel are studied in detail, so as to complete
The present invention.
That is, idea of the invention is formed as follows.
1. a kind of structural tube steel plate,
Formed with following composition：Contain C in terms of quality %：0.060~0.100%, Si：0.01~0.50%, Mn：
1.50~2.50%, Al：Less than 0.080%, Mo：0.10~0.50%, Ti：0.005~0.025%, Nb：0.005~
0.080%th, N：0.001~0.010%, O：Less than 0.0050%, P：Less than 0.010% and S：Less than 0.0010%, remainder
Divide and be made up of Fe and inevitable impurity, also,
The Ti contents that are represented by quality % with being 2.5~4.0 by the ratio between quality % N contents represented, i.e. Ti/N,
The carbon equivalent C defined by following (1) formulaseqFor more than 0.45,
The X defined by following (2) formulas is less than 0.30,
The Y defined by following (3) formulas is more than 0.15；
Also, it is main body and microstructure of the Line Integral rate less than 3.0% of island-like martensite with bainite；
Also, tensile strength (the TS of rolling directionL) it is more than 760MPa, roll the tensile strength (TS of orthogonal directionC) with
Tensile strength (the TS of rolling directionL) difference (TSC-TSL) absolute value be below 30MPa,
Ceq=C+Mn/6+ (Cu+Ni)/15+ (Cr+Mo+V)/5 ... (1)
(wherein, the symbol of element in (1) formula is the value for representing the content of each element in above-mentioned steel plate with quality %,
For 0) when not containing the element in the steel plate
X=(C+Mo/5)/Ceq…(2)
Y=[Mo]+[Ti]+[Nb]+[V] ... (3)
(wherein, [M] is the value for representing the content of the element M in above-mentioned steel plate with atom %, and member is not contained in the steel plate
It is [M]=0 during plain M)
2. the structural tube steel plate according to above-mentioned 1, wherein, mentioned component composition further contains V in terms of quality %：
0.005~0.100%.
3. the structural tube steel plate according to above-mentioned 1 or 2, wherein, mentioned component composition is further contained in terms of quality %
Have and be selected from Cu：Less than 0.50%, Ni：Less than 0.50%, Cr：Less than 0.50%, Ca：0.0005~0.0035%, REM：
0.0005~0.0100% and B：It is one kind or two or more in less than 0.0020%.
A kind of 4. manufacture method of structural tube steel plate, at least with following process：
Heating process, the steel billet material formed with the composition any one of above-mentioned 1~3 is heated until heating
Temperature：1100~1300 DEG C；
Hot-rolled process, hot rolling is carried out to heated steel billet material in above-mentioned heating process and steel plate is made；
Accelerate refrigerating work procedure, by the steel plate of above-mentioned hot rolling to cool down start temperature：The Ar defined by following formula3More than point,
Cool down end temp：Less than 300 DEG C, average cooling rate：20 DEG C/more than s condition accelerates cooling；
Reheating operation, after above-mentioned acceleration refrigerating work procedure, carried out again with 0.5 DEG C/s~10 DEG C/s programming rate immediately
Heat until 300~550 DEG C,
Ar3(DEG C)=910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
(wherein, the symbol of element in above-mentioned formula is the value for representing the content of each element in above-mentioned steel plate with quality %,
For 0) when not containing the element in the steel plate
5. a kind of structural tube, it is made up of the structural tube any one of above-mentioned 1~3 with steel plate.
6. a kind of structural tube, it is by the steel plate any one of above-mentioned 1~3 after long side direction is shaped to tubular, incites somebody to action
Docking section is from surfaces externally and internally obtained from least each 1 layer of long side direction welding.
It is high-strength steel sheet more than API X100 grades in accordance with the invention it is possible to provide a kind of structural tube steel plate,
The excellent strength of rolling direction in the case of substantial amounts of alloying element is not added, and rolling direction and rolling vertical direction is strong
Degree is poor small (property uniform in material is excellent).
Embodiment
[composition composition]
Next, the restriction reason of each constitutive requirements of the present invention is illustrated.
In this invention it is important that there is structural tube steel plate defined composition to form.Therefore, first, in this hair
The reasons why composition composition for limiting steel in bright as described above, illustrates.It should illustrate, " % " on composition is as long as represent
It is not particularly illustrated, means that " quality % ".
C：0.060~0.100%
C is the element for the intensity for increasing steel, in order to obtain desired tissue, be made desired intensity, toughness, it is necessary to
It is more than 0.060% to make C content.On the other hand, if C content is more than 0.100%, weldability deterioration, welding is easily produced
Crackle, and base metal tenacity and HAZ toughness reduce.Therefore, C content is less than 0.100%.It should illustrate, C content is preferably
0.060~0.080%.
Si：0.01~0.50%
Si is that the element of steel strength is played a role and increased by solution strengthening as deoxidier.It is above-mentioned in order to obtain
Effect, it is more than 0.01% to make Si contents.On the other hand, if Si contents substantially deteriorate more than 0.50%, HAZ toughness.Cause
This, Si contents are less than 0.50%.It should illustrate, Si contents are preferably 0.05~0.20%.
Mn：1.50~2.50%
Mn is quenching degree and the element of raising intensity and toughness for having the function that to improve steel.In order to obtain the effect above,
It is more than 1.50% to make Mn contents.On the other hand, if Mn contents are more than 2.50%, weldability is possible to deteriorate.Therefore, Mn
Content is less than 2.50%.It should illustrate, Mn contents are preferably 1.80%~2.00%.
Al：Less than 0.080%
Deoxidier when Al is as steel-making and the element that adds.If Al content causes toughness to drop more than 0.080%
It is low, therefore Al content is less than 0.080%.It should illustrate, Al content is preferably 0.010~0.050%.
Mo：0.10~0.50%
Mo is element especially important in the present invention, has following function：Suppress the pearlite during cooling after hot rolling
Phase transformation, while it is substantially increased the intensity of steel plate into fine double carbide with Ti, Nb, V-arrangement.In order to obtain above-mentioned effect
Fruit, it is more than 0.10% to make Mo contents.On the other hand, if Mo contents cause welding heat affected zone more than 0.50%
(Heat-Affected Zone, HAZ) toughness reduces, therefore Mo contents are less than 0.50%.
Ti：0.005~0.025%
Same with Mo, Ti is element especially important in the present invention, forms miscible precipitate with Mo and significantly contributes to
Improve the intensity of steel.In order to obtain the effect above, it is more than 0.005% to make Ti contents.On the other hand, adding more than 0.025%
Adding can cause HAZ toughness and base metal tenacity to deteriorate.Therefore, Ti contents are less than 0.025%.
Nb：0.005~0.080%
Nb is the element for having the function that to improve toughness by the micronized of tissue.In addition, formed together with Mo compound
Precipitate and be favorably improved intensity.In order to obtain the effect above, it is more than 0.005% to make Nb contents.On the other hand, if Nb
Content is more than 0.080%, then HAZ toughness deteriorates.Therefore, Nb contents are less than 0.080%.
N：0.001~0.010%
N is present in steel usually as inevitable impurity, if there is Ti, then forms TiN.In order to pass through TiN's
Pinning effect (Pinning effect) suppresses the coarsening of austenite crystal, and it is more than 0.001% to make N content.But
TiN is in weld part, the Region Decomposition for being heated to more than 1450 DEG C particularly near welded joint, generation solid solution N.Therefore,
If N content is too high, the reduction of toughness as caused by generating above-mentioned solid solution N becomes obvious.Therefore, N content 0.010%
Below.It should illustrate, N content is more preferably 0.002~0.005%.
In addition, being 2.5~4.0 by the Ti/N for making to be used as the ratio between Ti contents and N content, above-mentioned TiN can be given full play to
Effect.From the viewpoint of the pinning effect for more effectively playing above-mentioned TiN, Ti/N is preferably more than 2.6, additionally, it is preferred that
For less than 3.8.
O：Less than 0.0050%, P：Less than 0.010%, S：Less than 0.0010%
In the present invention, O, P and S are inevitable impurity, and the upper limit of the content of these elements is specified below.
O forms oxygen system that is thick and being adversely affected to toughness field trash.In order to suppress the influence of above-mentioned field trash, the O content is set to be
Less than 0.0050%.In addition, P has the property for carrying out center segregation and reducing the toughness of mother metal, so if P content is high,
Then base metal tenacity, which reduces, turns into problem.Therefore, P content is less than 0.010%.Form MnS systems field trash in addition, S has and make
The property that the toughness of mother metal reduces, so if S contents are high, then the reduction of base metal tenacity turns into problem.Therefore, S contents are
Less than 0.0010%.It should illustrate, O content is preferably less than 0.0030%, and P content is preferably that less than 0.008%, S contents are excellent
Elect less than 0.0008% as.On the other hand, the lower limit of O, P, S content is not limited, but industrially more than 0%.In addition, if excessively
Content is reduced, then can cause increase, the rising of cost of refining time, therefore O content is preferably more than 0.0005%, P content
Preferably more than 0.001%, S contents are preferably more than 0.0001%.
In addition, the present invention structural tube with steel plate in addition to above-mentioned element, can also further contain V：0.005~
0.100%.
V：0.005~0.100%
Same with Nb, V forms miscible precipitate together with Mo, contributes to intensity to rise.It is above-mentioned in order to obtain when adding V
Effect, it is more than 0.005% to make V content.On the other hand, if V content reduces more than 0.100%, HAZ toughness, therefore add
When adding V, it is less than 0.100% to make V content.
In addition, the structural tube of the present invention with steel plate in addition to above-mentioned element, can also be further containing being selected from Cu：0.50%
Below, Ni：Less than 0.50%, Cr：Less than 0.50%, Ca：0.0005~0.0035%, REM：0.0005~0.0100% and B：
It is one kind or two or more in less than 0.0020%.
Cu：Less than 0.50%
Cu is the effective element of raising of the improvement and intensity to toughness, but if addition is excessive, then weldability reduces.
Therefore, when adding Cu, Cu contents are less than 0.50%.It should illustrate, the lower limit of Cu contents is not particularly limited, but adds Cu
When, it is more than 0.05% preferably to make Cu contents.
Ni：Less than 0.50%
Ni is that but if addition is excessive, then resistance to PWHT characteristics reduce to improving toughness and improving the effective element of intensity.
Therefore, when adding Ni, Ni contents are less than 0.50%.It should illustrate, the lower limit of Ni contents is not particularly limited, but during addition Ni
It is preferred that Ni contents are made to be more than 0.05%.
Cr：Less than 0.50%
It is same with Mn, even if Cr is pair the effective element of enough intensity also to be obtained under low C, but it is excessively added and can reduces
Weldability.Therefore, when adding Cr, it is less than 0.50% to make Cr contents.It should illustrate, the lower limit of Cr contents is not particularly limited,
But it is more than 0.05% preferably to make Cr contents when adding Cr.
Ca：0.0005~0.0035%
Ca is to improving the effective element of toughness by controlling the form of sulfide-based field trash.In order to obtain above-mentioned effect
Fruit, when adding Ca, it is more than 0.0005% to make Ca contents.On the other hand, even if addition Ca is more than 0.0035%, effect is also satisfied
With on the contrary, reduce toughness because of the reduction of the cleannes of steel.Therefore, when adding Ca, it is less than 0.0035% to make Ca contents.
REM：0.0005~0.0100%
REM (rare earth metal) same with Ca is to improving toughness by controlling the form of the sulfide-based field trash in steel
Effective element.In order to obtain the effect above, when adding REM, it is more than 0.0005% to make REM contents.On the other hand, even if adding
Add more than 0.0100%, make when effect also saturation, on the contrary, reducing toughness because of the reduction of the cleannes of steel, therefore adding REM
REM contents are less than 0.0100%.
B：Less than 0.0020%
B suppresses ferrite transformation and is especially useful against HAZ intensity decreases because being segregated in austenite grain boundary.But
Even if addition, more than 0.0020%, its effect also saturation, therefore during addition B, B content is less than 0.0020%.It should illustrate, B
The lower limit of content is not particularly limited, but preferably makes B content be more than 0.0002% during addition B.
The structural tube of the present invention is made up of with steel plate composition above and the Fe of remainder and inevitable impurity.
Should illustrate, " remainder is made up of Fe and inevitable impurity " if represent do not damage the present invention action effect,
The scope of the present invention is also contained in containing other micro- situations using inevitable impurity as representative.
In this invention it is important that the element not only contained in steel meets above-mentioned condition respectively, and make by following (1)
The carbon equivalent C that formula defineseqFor more than 0.45.
Ceq=C+Mn/6+ (Cu+Ni)/15+ (Cr+Mo+V)/5 ... (1)
(wherein, the symbol of element in (1) formula represents represent the content of each element in above-mentioned steel plate with quality %
It is worth, for 0) when not containing the element in the steel plate
Above-mentioned CeqIt is that the influence for the element that will be added in steel is converted into the value of carbon amounts expression, it is relevant with strength of parent, therefore
Used generally as the index of intensity.In the present invention, in order to obtain high intensity more than API X100 grades, make CeqFor 0.45 with
On.It should illustrate, CeqPreferably more than 0.46.On the other hand, CeqThe upper limit be not particularly limited, but preferably less than 0.50.
In addition, in order to reduce the amount of the island-like martensite decomposed by PWHT, it is important that make to be defined by following (2) formulas
Parameter X is less than 0.30.
X=(C+Mo/5)/Ceq…(2)
Above-mentioned parameter X is relative to carbon equivalent CeqC and Mo ratio, if this 2 kinds of elements are excessive, easily formed island
Shape martensite.In the present invention, by accelerating the reheating after cooling down to suppress the formation of island-like martensite, but in order to as rule
The fixed island martensite scale of construction is, it is necessary to make parameter X be less than 0.30.It should illustrate, preferably less than 0.28, more preferably 0.27
Below.Parameter X lower limit is not particularly limited, but preferably more than 0.10.
In addition, in this invention it is important that the Y for making to be defined by following (3) formulas is more than 0.15.
Y=[Mo]+[Ti]+[Nb]+[V] ... (3)
(wherein, [M] is the value for representing the content of the element M in above-mentioned steel plate with atom %, and member is not contained in the steel plate
It is [M]=0 during plain M)
Above-mentioned Y is the index of precipitation strength, in the present invention, in order to obtain high intensity more than API X100 grades, makes the Y be
More than 0.15.It should illustrate, Y is preferably more than 0.18%.On the other hand, the Y upper limit is not particularly limited, but preferably 0.50
Below.
It should illustrate, the Y defined by above-mentioned (3) formula value, i.e. Mo, Ti, Nb and V each element are represented by atom %
The total of content be whole elements by containing in the atomicity sum divided by steel by Mo, Ti, Nb and V for containing in steel
Atomicity and obtain, but Mo, Ti, Nb and V can also be used to be obtained by following (4) formulas by the content that quality % is represented.
Y=(Mo/95.9+Nb/92.91+V/50.94+Ti/47.9)/(100/55.85) × 100 ... (4)
(wherein, the symbol of element in (4) formula represents represent the content of each element in above-mentioned steel plate with quality %
It is worth, for 0) when not containing the element in the steel plate
[microstructure]
Next, the restriction reason of the tissue of the steel in the present invention is illustrated.
In this invention it is important that there is steel plate bainite to be less than for the Line Integral rate of main body and island-like martensite
3.0% microstructure.By so controlling microstructure, the high intensity of API X100 grades can be realized.It should illustrate, such as
The microstructure of fruit thickness of slab central part meets above-mentioned condition, then the almost whole region in the thickness of slab direction of steel plate, which has, meets
The microstructure of condition is stated, so as to embody the effect of the application.
Here, microstructure is the Line Integral that " bainite is main body " represents bainite shared in the microstructure of steel
Rate is more than 80%.It should illustrate, the Line Integral rate of bainite is more preferably more than 90%.On the other hand, the area of bainite
Divide the total more high more preferred of rate, therefore the upper limit is not particularly limited, and can be 100%.
Tissue beyond bainite is more few better, but as long as the area occupation ratio of bainite is sufficiently high, then the tissue of remainder
Influence just can almost ignore, therefore allow in the tissue in terms of adding up to area occupation ratio beyond the bainite containing less than 20%
It is one kind or two or more.Tissue beyond these bainites is preferably calculated as less than 10% with total area occupation ratio.It is grouped as remainder
The example knitted, pearlite, cementite, ferrite, martensite etc. can be enumerated.
But even if it is main body that microstructure, which is bainite, but if wherein containing island-like martensite, then the island in PWHT
Shape martensite decomposes and intensity can reduce.Therefore, it is necessary to make island-like martensite Line Integral shared in the microstructure of steel plate
Rate is less than 3.0%.It should illustrate, the Line Integral rate of island-like martensite is preferably less than 2%.On the other hand, island-like martensite
Line Integral rate is more low more preferred, therefore lower limit is not particularly limited, and can be more than 0%.
It should illustrate, the Line Integral rate of bainite and island-like martensite can be entered to the sample taken from thickness of slab center
The face that row mirror ultrafinish, the corrosion of nitric acid alcohol form, 10 are carried out using sweep electron microscope (2000 times of multiplying power) at random
More than visual field observation is identified.
[mechanical property]
The structural tube steel plate of the present invention has following mechanical property：Tensile strength (the TS of rolling directionL) it is 760MPa
More than, roll the tensile strength (TS of orthogonal directionC) with the tensile strength (TS of rolling directionL) difference (TSC- TSL) it is absolute
It is worth for below 30MPa.Here, TSLAnd TSCIt can be determined with the method described in embodiment.It should illustrate, TSLPreferably
More than 790MPa, (TSC- TSL) absolute value be preferably below 20MPa.On the other hand, TSLThe upper limit be not particularly limited, example
Such as, then it is below 990MPa if X100 grades, is then below 1145MPa if X120 grades.(TSC-TSL) it is exhausted
It is smaller more preferred to being worth, therefore lower limit is not particularly limited, and can be more than 0.It should illustrate, from TSCSubtract TSLObtained by value
(TSC- TSL) can be negative.
For the structural tube steel plate of the present invention, as described above, because TSCWith TSLDifference it is small, so using the steel plate system
The steel pipe made has as structural tube can easily realize the overmatch of seam weld connector portions and circumference soldering connector portions so
Extremely excellent characteristic.
[manufacture method of steel plate]
Next, the manufacture method of the steel plate of the present invention is illustrated.It should illustrate, in the following description, as long as
It is not particularly illustrated, temperature is exactly the mean temperature in the thickness of slab direction of steel plate.The mean temperature in the thickness of slab direction of steel plate is according to plate
Thick, surface temperature and cooling condition etc. are obtained by simulating calculating etc..For example, thickness of slab direction is calculated by using calculus of finite differences
Temperature Distribution, so as to obtain the mean temperature in the thickness of slab direction of steel plate.
The present invention structural tube with steel plate can by the steel billet material to being formed with mentioned component according to following (1)~
(4) process is handled to manufacture successively.
(1) heating process, above-mentioned steel billet material is heated to heating-up temperature：1100~1300 DEG C；
(2) hot-rolled process, hot rolling is carried out to the steel billet material heated in above-mentioned heating process and steel plate is made；
(3) refrigerating work procedure is accelerated, by above-mentioned hot rolled steel plate to cool down start temperature：Ar3More than point, cool down and terminate temperature
Degree：Less than 300 DEG C, average cooling rate：20 DEG C/more than s condition accelerates cooling；With
(4) reheating operation, after above-mentioned acceleration refrigerating work procedure, entered immediately with 0.5 DEG C/s~10 DEG C/s programming rate
Row is reheated until 300~550 DEG C.
Specifically, above-mentioned each operation can be carried out as described below.
[steel billet material]
Above-mentioned steel billet material can conventionally carry out melting.The manufacture method of steel billet material is not particularly limited, preferably
Manufactured using continuous casting process.
[heating process]
Above-mentioned steel billet material first heats before the rolling.Heating-up temperature now is 1100~1300 DEG C.By making heating-up temperature
For more than 1100 DEG C, the carbide in steel billet material can be dissolved and ensure target strength.It should illustrate, above-mentioned heating-up temperature is excellent
Elect more than 1120 DEG C as.On the other hand, if heating-up temperature is more than 1300 DEG C, austenite crystal coarsening, final steel group
Knit also coarsening and toughness deteriorates, therefore heating-up temperature is less than 1300 DEG C.It should illustrate, above-mentioned heating-up temperature is preferably 1250
Below DEG C.
[hot-rolled process]
Next, the steel billet material heated in above-mentioned heating process is rolled.The condition of hot rolling is not particularly limited,
But in order to as aftermentioned from Ar3The point above is that austenite one phase area starts to accelerate cooling, preferably in Ar3More than point terminate to roll.
[acceleration refrigerating work procedure]
After hot-rolled process terminates, acceleration cooling is carried out to the steel plate obtained in the hot-rolled process.Now, if from less than
Ar3The coexistence region of point is begun to cool down, then the microstructure being mixed as ferrite, the intensity decreases of steel plate.Therefore, from Ar3
The point above is that austenite one phase area starts to accelerate cooling.It should illustrate, the upper limit for cooling down start temperature is not particularly limited, but excellent
Elect (Ar as3+ 100) below DEG C.
It should illustrate, in the present invention Ar3Point is calculated by following formula.
Ar3(DEG C)=910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
(wherein, the symbol of element in above-mentioned formula is the value for representing the content of each element in above-mentioned steel plate with quality %,
For 0) when not containing the element in the steel plate
In addition, if cooling end temp is too high, then the phase transformation to bainite can not be fully carried out, largely generates pearly-lustre
Body, MA, it is possible to adversely affected to toughness.Therefore, cool down end temp and be less than 300 DEG C.It should illustrate, cooling terminates temperature
The lower limit of degree is not particularly limited, but preferably more than 100 DEG C.
In addition, when average cooling rate is low, the phase transformation to bainite also can not be fully carried out, largely generates pearlite,
It is possible to adversely affect toughness.Therefore, average cooling rate is 20 DEG C/more than s.It should illustrate, average cooling rate
The upper limit be not particularly limited, preferably 40 DEG C/below s.
By carrying out acceleration cooling with above-mentioned condition, the microstructure of steel plate can be made as bainite to be main body, improved
Intensity.
[reheating operation]
After above-mentioned acceleration cooling terminates, reheated immediately until 300 with 0.5 DEG C/s~10 DEG C/s programming rate~
550℃.By being reheated with above-mentioned condition, mobile dislocation is fixed by solid solution C, and it is excellent as a result can to obtain property uniform in material
Steel plate.Its effect is small when relation reheating temperature is less than 300 DEG C, produces material qualitative difference.On the other hand, relation reheating temperature exceedes
At 550 DEG C, it is possible to cause the deterioration of toughness because excessively separating out.Here, refer to accelerate cooling knot " after accelerating cooling, immediately "
Shu Hou, started the reheating of 0.5 DEG C/s~10 DEG C/s programming rate within 120 seconds.
By above process, can manufacture with high intensity more than API X100 grades and the excellent knot of property uniform in material
The effective steel plate of structure.Particularly, by Application of composite because accelerate cool down when bainitic transformation caused by phase transformation strengthening and because accelerate
Precipitation strength caused by the fine carbide separated out during reheating after cooling, it can not largely add the situation of alloying element
Under obtain excellent intensity.Therefore, in this invention it is important that meeting above-mentioned acceleration cooling condition and reheating condition simultaneously
Both.
It should illustrate, the thickness of steel plate is not particularly limited, and can be any thickness, but preferably 15~30mm.
[steel pipe]
The steel plate obtained as described above can be used as blank material and manufacture steel pipe.Above-mentioned steel pipe can for example be made by
The effective thick steel sheet of said structure is in the structural tube that long side direction is shaped to tubular, butt welding portion forms.System as steel pipe
Method is made, is not particularly limited, any means can be used.Such as can be conventionally with U-shaped forcing press and O-shaped pressure
Machine by steel plate plate long side direction formed tubular after, seam weld docking section and UOE steel pipes are made.Above-mentioned seam weld is preferably in positioning welding
Inner surface, outer surface are with least each 1 layer of progress submerged-arc welding afterwards.The solder flux used in submerged-arc welding is not particularly limited, can
Think fusion solder flux, or sinter molding flux.After carrying out seam weld, in order to remove weld residual stress and improve steel pipe
Out of roundness, implement expander.In expansion process pipe expanding rate (external diameter of external diameter variable quantity before and after expander and the pipe before expander it
Than) generally 0.3%~1.5% scope implement.From the balance of the ability required by out of roundness improvement and pipe expander
From the viewpoint of, pipe expanding rate is preferably 0.5%~1.2% scope.Above-mentioned UOE techniques can be replaced, using anti-to steel plate
Carry out three-point bending again and pressure bending (Press Bend) method that is gradually molded manufactures the cross sectional shape with circular
Steel pipe after, implement seam weld in the same manner as above-mentioned UOE techniques., can also be with UOE techniques in the case of pressure bending method
Situation carries out expander after similarly carrying out seam weld.Pipe expanding rate is (before the external diameter variable quantity and expander before and after expander in expansion process
The ratio between the external diameter of pipe) scope generally 0.3%~1.5% implemented.Required by out of roundness improvement and pipe expander
Ability balance from the viewpoint of, pipe expanding rate is preferably 0.5%~1.2% scope.In addition, as needed, it can also enter
The heat treatment after preheating or welding before row welding.
Embodiment
The steel (steel grade A~M, remainder are iron and inevitable impurity) formed to the composition shown in table 1 is carried out
Melting, slab is made using continuous casting process.Obtained slab is heated, hot rolling, thereafter, immediately using water-cooling type plus
Fast cooling device is cooled down to manufacture thickness of slab 20mm steel plate (No.1~19).The manufacturing condition of each steel plate is shown in table 2.Profit
The area of island-like martensite shared in microstructure and bainite is each carried out to obtained steel plate with method described below
Divide the evaluation of rate and mechanical property.Evaluation result is shown in table 3.
For the Line Integral rate of island-like martensite and bainite, using sweep electron microscope (2000 times of multiplying power) to inciting somebody to action
The sample taken from thickness of slab center carries out mirror ultrafinish, the face sight more than 10 visual fields of progress at random of nitric acid alcohol corrosion
Examine and evaluate.
0.5% endurance (YS) and tensile strength (TS) in mechanical property are to rolling vertical direction (C directions) and rolling
What both directions (L directions) were measured.In measure, rolling direction and the respective complete thick examination of vertical direction are taken from steel plate
Piece is tested, implements tension test according to JIS Z 2241 (1998) regulation.
For the Charpy characteristic in mechanical property, respectively taking 3 from thickness of slab central part makes rolling direction for long side direction
2mmV type breach Charpy test pieces, Charpy when -10 DEG C are determined to each test film absorb energy (vE-10℃), obtain the flat of them
Average.
In addition, in order to evaluate welding heat affected zone (HAZ) toughness, using reappear device heat cycle make be applied with equivalent to
The test film of heat input 20kJ/cm~50kJ/cm thermal history, Charpy-type test is carried out using obtained test film.Utilize
The evaluation identical method that energy is absorbed with Charpy at above-mentioned -10 DEG C is measured, and Charpy at will obtain -10 DEG C absorbs
Energy is that more than 100J situation is evaluated as good (zero), and the situation less than 100J is evaluated as bad (×).
In addition, in order to evaluate resistance to PWHT characteristics, the PWHT of each steel plate is carried out using gas atmosphere stove.Heat treatment bar now
Part is 2 hours at 600 DEG C, thereafter, steel plate is taken out from stove, room temperature is cooled to using air cooling.Using with before above-mentioned PWHT
Measure identical method determine 0.5%YS, TS and vE of rolling direction respectively to the steel plate after obtained PWHT-10℃。
As shown in table 3, meet that the example (No.1~7) of the condition of the present invention in the state of carrying out before PWHT, possesses
Yield strength (0.5%YSC) it is more than 690MPa, tensile strength (TSC) for more than 760MPa excellent intensity and roll it is orthogonal
Tensile strength (the TS in directionC) with the tensile strength (TS of rolling directionL) difference (TSC-TSL) it is that below 30MPa is such excellent
Property uniform in material, and also possess excellent mechanical property after the PWTH at a high temperature of 600 DEG C.In addition, the steel of example
The Charpy characteristic (toughness) of plate is vE well-10℃：More than 200J, moreover, HAZ toughness is also good.
On the other hand, be unsatisfactory for the present invention condition comparative example (No.8~20) in, before PWTH and PWTH after in
The mechanical property of one or both, property uniform in material are poor.For example, the steel of No.8,12,13 into being grouped into the scope of the present invention
It is interior, but strength of parent or base metal tenacity are poor.It is thought that because condition when manufacturing is unsatisfactory for the condition of the present invention, therefore it is fine
Carbide is not dispersed to precipitate suitably.In addition, No.9 steel into being grouped into the scope of the present invention, but cool down and start temperature
Degree is unsatisfactory for the condition of the present invention, therefore ferritic structure is mixed in steel plate microstructure, as a result, before and after PWHT
Mechanical properties.No.10,11 steel into being grouped into the scope of the present invention, but the island martensite in steel plate microstructure
The Line Integral rate of body is more than 3.0%, as a result, the intensity difference after the Charpy characteristic of mother metal steel plate, PWHT.On the other hand, No.14
~19 steel into being grouped into outside the scope of the present invention, therefore the intensity after strength of parent, Charpy characteristic, HAZ toughness, PWHT
At least one of difference.
Table 2
Industrial applicability
It is high-strength steel sheet more than API X100 grades in accordance with the invention it is possible to provide a kind of structural tube steel plate, and
The excellent strength of rolling direction in the case where not adding a large amount of alloying elements, and rolling direction is with rolling the strong of vertical direction
Degree is poor small (property uniform in material is excellent).It is special that the structural tube obtained using above-mentioned steel plate also maintains excellent machinery after PWHT
Property, therefore be exceedingly useful as structural tubes such as conductor casing steel pipe, the standpipe steel pipes for being possible to carry out PWHT.
Claims (6)
1. a kind of structural tube steel plate,
Formed with following composition：Contained in terms of quality %
C：0.060~0.100%,
Si：0.01~0.50%,
Mn：1.50~2.50%,
Al：Less than 0.080%,
Mo：0.10~0.50%,
Ti：0.005~0.025%,
Nb：0.005~0.080%,
N：0.001~0.010%,
O：Less than 0.0050%,
P：Less than 0.010% and
S：Less than 0.0010%,
Remainder is made up of Fe and inevitable impurity,
And the Ti contents represented by quality % with by the ratio between the quality % N contents represented i.e. Ti/N be 2.5~4.0,
The carbon equivalent C defined by following (1) formulaseqFor more than 0.45,
The X defined by following (2) formulas is less than 0.30,
The Y defined by following (3) formulas is more than 0.15,
Also, it is the microstructure of main body and the Line Integral rate of island-like martensite less than 3.0% with bainite,
Also, the tensile strength TS of rolling directionLFor more than 760MPa, the tensile strength TS of orthogonal direction is rolledCWith rolling direction
Tensile strength TSLDifference TSC-TSLAbsolute value be below 30MPa,
Ceq=C+Mn/6+ (Cu+Ni)/15+ (Cr+Mo+V)/5 ... (1)
Wherein, the symbol of element in (1) formula is the value that represents the content of each element in the steel plate with quality %, the steel plate
In be 0 when not containing the element,
X=(C+Mo/5)/Ceq…(2)
Y=[Mo]+[Ti]+[Nb]+[V] ... (3)
Wherein, [M] is the value for representing the content of the element M in the steel plate with atom %, when not containing element M in the steel plate
For [M]=0.
2. structural tube steel plate according to claim 1, wherein, the composition composition further contains V in terms of quality %：
0.005~0.100%.
3. structural tube steel plate according to claim 1 or 2, wherein, the composition composition is further contained in terms of quality %
It is selected from
Cu：Less than 0.50%,
Ni：Less than 0.50%,
Cr：Less than 0.50%,
Ca：0.0005~0.0035%,
REM：0.0005~0.0100% and
B：It is one kind or two or more in less than 0.0020%.
A kind of 4. manufacture method of structural tube steel plate, at least with following process：
Heating process, the steel billet material formed with composition according to any one of claims 1 to 3 is heated to heating-up temperature：
1100~1300 DEG C,
Hot-rolled process, hot rolling is carried out to the steel billet material heated in the heating process and steel plate is made,
Accelerate refrigerating work procedure, by the steel plate of the hot rolling to cool down start temperature：The Ar defined by following formula3More than point, cool down knot
Shu Wendu：Less than 300 DEG C, average cooling rate：20 DEG C/more than s condition accelerates cooling, and
Reheating operation, after the acceleration refrigerating work procedure, with 0.5 DEG C/s~10 DEG C/s programming rate again add immediately
Heat to 300~550 DEG C,
Ar3(DEG C)=910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
Wherein, the symbol of element in the formula is the value that represents the content of each element in the steel plate with quality %, the steel
It is 0 when the element is not contained in plate.
5. a kind of structural tube, it is made up of structural tube according to any one of claims 1 to 3 with steel plate.
6. a kind of structural tube, it is that structural tube according to any one of claims 1 to 3 is shaped to cylinder with steel plate in long side direction
After shape, docking section is welded obtained from least each 1 layer from surfaces externally and internally in long side direction.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JPPCT/JP2015/001753 | 2015-03-26 | ||
| JP2015001753 | 2015-03-26 | ||
| PCT/JP2016/001764 WO2016152171A1 (en) | 2015-03-26 | 2016-03-25 | Steel plate for structural pipe, method for producing steel plate for structural pipe, and structural pipe |
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| Publication Number | Publication Date |
|---|---|
| CN107429351A true CN107429351A (en) | 2017-12-01 |
Family
ID=56977194
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201680017746.0A Pending CN107429351A (en) | 2015-03-26 | 2016-03-25 | The manufacture method and structural tube of structural tube steel plate, structural tube steel plate |
Country Status (8)
| Country | Link |
|---|---|
| US (1) | US20180298460A9 (en) |
| EP (1) | EP3276025B1 (en) |
| JP (1) | JP6256653B2 (en) |
| KR (1) | KR101993201B1 (en) |
| CN (1) | CN107429351A (en) |
| CA (1) | CA2980250C (en) |
| RU (1) | RU2679499C1 (en) |
| WO (1) | WO2016152171A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113646455A (en) * | 2019-03-28 | 2021-11-12 | 杰富意钢铁株式会社 | Steel material for line pipe, method for producing same, line pipe, and method for producing same |
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| JP6245352B2 (en) * | 2014-03-31 | 2017-12-13 | Ｊｆｅスチール株式会社 | High-tensile steel plate and manufacturing method thereof |
| CN107429354B (en) | 2015-03-27 | 2020-06-09 | 杰富意钢铁株式会社 | High-strength steel and method for producing same, and steel pipe and method for producing same |
| CN116162857A (en) | 2015-07-27 | 2023-05-26 | 杰富意钢铁株式会社 | High-strength hot-rolled steel sheet and method for producing same |
| KR102457409B1 (en) * | 2018-06-29 | 2022-10-24 | 닛폰세이테츠 가부시키가이샤 | steel pipe and plate |
| EP3831971B1 (en) * | 2018-07-31 | 2023-03-15 | JFE Steel Corporation | High-strength hot-rolled plated steel sheet |
| KR102209581B1 (en) * | 2018-11-29 | 2021-01-28 | 주식회사 포스코 | The steel plate having excellent heat affected zone toughness and method for manufacturing thereof |
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Also Published As
| Publication number | Publication date |
|---|---|
| RU2679499C1 (en) | 2019-02-11 |
| KR20170130484A (en) | 2017-11-28 |
| KR101993201B1 (en) | 2019-06-26 |
| JPWO2016152171A1 (en) | 2017-06-15 |
| EP3276025A1 (en) | 2018-01-31 |
| US20180298460A9 (en) | 2018-10-18 |
| JP6256653B2 (en) | 2018-01-10 |
| WO2016152171A1 (en) | 2016-09-29 |
| US20180057905A1 (en) | 2018-03-01 |
| EP3276025A4 (en) | 2018-01-31 |
| CA2980250A1 (en) | 2016-09-29 |
| EP3276025B1 (en) | 2019-05-01 |
| CA2980250C (en) | 2020-03-10 |
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